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Front. Mater., 27 November 2020
Sec. Ceramics and Glass
Volume 7 - 2020 |

The Influence of Si3N4w Volume Fraction on the Microstructure and Properties of Si3N4w/Si3N4 Composites via CVI Technique

www.frontiersin.orgChao Chen1 www.frontiersin.orgYongsheng Liu1,2* www.frontiersin.orgWei Yue1 www.frontiersin.orgFang Ye1 www.frontiersin.orgJing Wang1 www.frontiersin.orgQingfeng Zeng1
  • 1Science and Technology on Thermostructural Composite Materials Laboratory, Northwestern Polytechnical University, Xi’an, China
  • 2NPU-SAS Joint Research Center of Advanced Ceramics, Northwestern Polytechnical University, Xi’an, China

Wave-transparent ceramic composites with excellent comprehensive performances are of particular significance for the development of space vehicles. In this study, Si3N4w was prepared by the gel-casting process and then combined with chemical vapor infiltration (CVI)-obtained Si3N4 to yield Si3N4w/Si3N4 composites with five Si3N4w volume fractions. The influence of the Si3N4w volume fraction on the microstructures, mechanical properties, and dielectric characteristics of the Si3N4w/Si3N4 composites were all studied. The results showed that Si3N4w/Si3N4 composites possess A sandwich structures. Higher Si3N4w volume fractions led to less incorporated amounts of the Si3N4 matrix at the same depth. The 25 vol% Si3N4w/Si3N4 composites integrated relatively higher Si3N4w volume fraction and load transfer ability of the matrix, leading to better flexural strengths reaching up to 41.37 MPa. The dielectric constants of the five prepared Si3N4w/Si3N4 composites ranged from 2.25 to 4.0. The dielectric losses were all lower than 0.005, demonstrating the good dielectric properties of the Si3N4w/Si3N4 composites.


High-temperature wave-transparent materials are used in spacecraft radomes and antenna windows, which require good mechanical and dielectric properties, as well as high-temperature resistance. Therefore, the development of novel wave-transparent materials with elevated wave transmittance and strength is of great significance for advanced and reliable applications (Medding, 1996; Bolivar et al., 2003; Ashok et al., 2007; Kandi et al., 2014; Hehdari et al., 2017).

Si3N4-based ceramics are employed in wave-transparent materials due to their excellent comprehensive performances (Arakawa et al., 1991; Hsieh and Mizuhara, 1987; Hsieh, 1987; Zou et al., 2009). For instance, Xu et al. (2020) studied the influence of different sintering additives on the dielectric properties of reaction-bonded Si3N4. Their results showed that the addition of Y2O3 and La2O3 powders may generate Y-Si-O-N and La-Si-O-N phases, further increasing the dielectric constant and dielectric loss Lee et al. (2000) prepared a Si3N4w/Si3N4 composite by the Gas Pressure Sintering (GPS) method. The amount of β-Si3N4w changed the microstructure, which changed the thermal conductivity. Ding et al. (2007) sintered Si3N4 powders at 1,200–1,500°C under air to yield prepared Si3N4 ceramics with a SiO2 coating on the surface. The influence of sintering temperature and holding time on the oxidation degree, porosity, flexural strength, and dielectric properties were all studied. The highest flexural strength of prepared Si3N4 ceramics reached 136.9 MPa and the lowest dielectric constant was 3.1.

To synergistically improve the mechanical and dielectric properties, the development of silicon nitride-based wave-transparent composite materials is increasingly considered (Cao et al., 2013; Wan et al., 2016). For example, Yang et al. (2019) (Li et al., 2019) prepared unidirectional silicon nitride fiber-reinforced silica composites by monofilament winding combined with the sol-gel method. The composite prepared by sintering under an N2 atmosphere showed the highest flexural strengths reaching up 210 MPa at 1,200°C. Besides, the flexural strength improved from 160 to 210 MPa at 900°C due to the release of stress in the fiber. Meanwhile, a Si3N4f/SiON/SiO2 composite has been prepared by introducing a SiON interphase using the precursor transformation method. After decarbonization by annealing, the flexural strength of Si3N4f/SiON/SiO2 decreased by 35% when compared to Si3N4f/SiO2 but the fracture toughness improved. Cheng et al. (2019) assembled porous Si3N4/Si3N4 composites by 3D printing combined with the chemical vapor infiltration (CVI) method. The increase in CVI processing to 12 h led to a decline in the porosity from 68.65 to 12.07. Meanwhile, the dielectric constant increased from 1.72 to 3.6 but the dielectric loss was always lower than 0.01. Since 2003, polysilazane has been used as a precursor in combination with the polymer infiltration pyrolysis process to prepare SiO2f/Si3N4 with good mechanical and high-temperature dielectric properties (Qi et al., 2005a; Qi et al., 2005b; Qi et al., 2005c).

However, extremely high or low volume fractions of reinforcement in the ceramic matrix composites should lead to the declined mechanical properties of the resulting composite materials. Besides, different reinforcement volume fractions should result in variable contents and distributions of reinforcement, as well as various matrices and pores, further influencing the dielectric properties of the composites. Therefore, clarifying the influencing rules of the reinforcement volume fractions on the mechanical and dielectric properties of ceramic matrix composites is highly desirable for advanced applications.

Li et al. (2020) prepared zirconia fiber hybrid alumina fiber/boron phenolic (ZA/BPF) composites with fiber volume fractions of 5, 10, 15, 25, and 30 vol%. The microscopic results showed that extremely low and high reinforcement volume fractions resulted in weak bonding between the matrix and fiber. At a fiber volume fraction of 25%, the maximum flexural strengths of the composites reached 48.86 MPa. Using the hot-pressing sintering method, Xu et al. (1994) prepared SiCf/Si3N4 with a fiber volume fraction of 14, 29, and 55 vol%. Their data suggested that the flexural strength of the composites first increased with the fiber volume fraction and then decreased. The reason for the reduction in strength was related to the fiber damage caused by its contact during the hot-pressing process of high volume fraction composites.

In this work, five preforms of Si3N4w volume fractions (5, 15, 25, 35, and 45 vol%) were prepared by the gel-casting process. Different volume fractions of the Si3N4w/Si3N4 composites were then obtained by introducing a Si3N4 matrix through the CVI Si3N4 process. The effects of whisker volume fractions on the microstructures, mechanical properties, and dielectric characteristics of the Si3N4w/Si3N4 composites were all studied. The results suggested that the 25 vol% Si3N4w/Si3N4 possessed the highest comprehensive performances.


Raw Materials

Water-based gel casting was used to prepare the Si3N4w preforms with different volume fractions. Firstly, Si3N4w was used to configure the Si3N4w slurry, then PMMA was added after ball milling for 4 h. Subsequently, the slurry was heated at 70°C to cure for 2 h. After drying, it was discharged at 400°C to create the Si3N4w performs. Si3N4w with a length of 4–12 μm (average 8 μm), diameter of 0.8–1.2 μm (average 1 μm), and average aspect ratio of 8:1 was prepared in our laboratory. Polymethyl methacrylate (PMMA; Wuhan Yuancheng Technology Development Co., Ltd.) was employed as the pore former, acrylamide (Tianjin Comeo Chemical Reagent Co., Ltd.) as a monomer, and methylenebisacrylamide (MACLIN) as a crosslinking agent.

SiCl4-NH3-H2-Ar was utilized as a gas source system for the preparation of the Si3N4 matrix by CVI, SiCl4 as a source of Si element, and H2 as a carrier and dilution gas. In this process, H2 was passed through the liquid SiCl4 to take the saturated SiCl4 vapor into the reaction furnace in actual production. NH3 was employed as a source of N element and Ar as a dilution gas. SiCl4, H2, and Ar with a purity of 99.999 vol% were all obtained from the Sichuan Messer Gas Products Co., Ltd., Xi’an branch. NH3 (purity 99.99 vol%) was purchased from the Beijing Marty Technology Co., Ltd.

Experimental Process

Sizing agents with Si3N4w volume fractions of 5, 15, 25, 35, and 45 vol% were prepared to yield preforms with Si3N4w volume fractions of 10, 20, 30, 40, and 50 vol% after solidification and decarbonization processes, respectively. To prevent over-shrinkage during the preparation of preforms at low volume fractions of Si3N4w, PMMA was added as a pore former in the sizing agent.

Using the CVI Si3N4 process, Si3N4w/Si3N4 composites with five-volume fractions of Si3N4w preforms were prepared and placed in the graphite mold. The CVI process are described in detail in literature (Zhou et al., 2019a). The preparation process was divided into six periods, each consisting of 60 h. For the convenience of subsequent expressions, the abbreviation 15 vol% Si3N4w/Si3N4 represented the composite prepared using the size agent with 15 vol% Si3N4w, the same as the other composites. The influences of volume fractions of Si3N4w on the microstructures, mechanical properties, and dielectric characteristics of Si3N4w/Si3N4 were all studied.


The density and porosity of each sample were tested by the Archimedes drainage method using AG204 electronic analytic balance by Mettler Toledo (accuracy 0.0001 g). The microstructures were viewed by a Helios G4 CX focused ion-electron double beam electron microscope (FEI). The flexural strength and fracture toughness values at loading speeds of 0.5 and 0.05 mm/min were obtained by the SANS CMT4304 electronic universal testing machine. The dielectric properties were tested by a vector network analyzer (MS4644A, produced by Anritsu, Japan). The experiments were performed at a standard dielectric sample size of 22.86 mm × 10.16 mm × h mm and a testing frequency band of 8.2–12.4 GHz.

Results and Discussion


The morphology of the Si3N4w preform before decarbonization is shown in Figure 1. The macro photo of the Si3N4w preform before decarbonization displayed a polymer matrix composite of certain strength and hardness, and it can be transferred without being destroyed after forming (Figures 1A). The smooth and flat surface revealed the advantages of the gel-casting in terms of near net-size forming. The high magnification SEM photo in Figures 1B exhibits the intact structures of Si3N4w and PMMA. The PMMA sphere with a diameter of approximately 5 μm could support the whisker structure. The low magnification SEM photo in Figures 1C reveals evenly dispersed dSi3N4w and PMMA, beneficial to the formation of connected pores after decarbonization.


FIGURE 1. Morphology of the Si3N4w preform before decarbonization: (A) macro photo; (B) high magnification SEM photo of section; (C) low magnification SEM photo of section.

The morphology of the Si3N4w preform after decarbonization is shown in Figure 2. The preform kept a perfectly consistent appearance during the decarbonization process (Figures 2A). In the SEM photo of Figures 2B, the shape of Si3N4w was completely preserved and the PMMA spheres were fully decomposed.


FIGURE 2. Morphology of Si3N4w after decarbonization: (A) macro photo; (B) SEM photo.

The Si3N4w volume fractions, bulk densities, and open porosities of the five prepared Si3N4w preforms after decarbonization are listed in Table 1. The Si3N4w volume fractions of the five preforms all increased due to the inevitable shrinkage during the solidification and decarbonization processes. Lower Si3N4w volume fractions in the sizing agent led to larger increasing rates of Si3N4w volume fractions in the preforms after decarbonization. In turn, the increase in the actual Si3N4w volume fraction in the preform led to a rise in bulk density from 0.42 to 1.50 g/cm3. By comparison, the open porosity declined from 86.5 to 52.7 vol%. The close porosity of the five preforms were all approximately 1 vol%, confirming the high connectivity of pores inside the preforms.


TABLE 1. Si3N4w volume fraction, bulk density, and open porosity of the five kinds of Si3N4w preform after decarbonization.

The weight increasing rates of five Si3N4w/Si3N4 composites are presented in Figure 3. All Si3N4 matrices were almost incremented in the first furnace deposition. Thus, the diffusion channels of deposition gas in the preforms became closed after the process. The subsequent deposition process ensured complete densification of all five Si3N4w/Si3N4 under the deposition conditions. Lower Si3N4w volume fractions led to larger weight increasing rates of Si3N4w/Si3N4, as well as significant differences between different Si3N4w/Si3N4. The weight increasing rate of 5 vol% Si3N4w/Si3N4 in the first furnace deposition reached 200.85%, while that of 45 vol% Si3N4w/Si3N4 was only 5.09%. The reason for this had to do with the light weight and large porosity of the low Si3N4w volume fraction composite.


FIGURE 3. Weight increase rate of five kinds of Si3N4w/Si3N4.

The bulk densities and open porosities of five prepared Si3N4w/Si3N4 composites are depicted in Figure 4. The bulk density of 5 vol% Si3N4w/Si3N4 was larger than that of 15 vol% Si3N4w/Si3N4. For other samples, larger Si3N4w volume fractions induced elevated bulk densities. The highest bulk density was recorded with 45 vol% Si3N4w/Si3N4 (1.65 g/cm3), while the lowest was obtained with 15 vol% Si3N4w/Si3N4 (1.06 g/cm3). The general rule of open porosity stated that higher Si3N4w volume fractions should yield larger open porosities. However, the high open porosity of 45 vol% Si3N4w/Si3N4 appeared to contradict the low porosity and small pore size of the 45 vol% Si3N4w preform.


FIGURE 4. Bulk density and open porosity of five kinds of Si3N4w/Si3N4.

To explain the above abnormal phenomenon, the surface morphologies of 45 and 25 vol% Si3N4w/Si3N4 were studied and the results are gathered in Figure 5. Numerous cracks were distributed on the surface of 45 vol% Si3N4w/Si3N4 (Figures 5B). The widths of the cracks were around 100 nm (Figures 5B). However, no cracks were noticed on the surface of 25 vol% Si3N4w/Si3N4 (Figures 5C, D). Therefore, the surface cracks caused the elevated open porosity of 45 vol% Si3N4w/Si3N4. The difference between the crystalline Si3N4w and amorphous CVI Si3N4 matrix (Zhou et al., 2019b) should induce differences between the thermal expansion coefficients of Si3N4w and the Si3N4 matrix. Elevated Si3N4w volume fractions yielded larger differences. Thus, high Si3N4w volume fraction composites were more prone to surface cracking. The existence of surface cracking would inevitably cause stress concentration and high open porosity, which would decline the ability of rain erosion resistance. On the other hand, the thermal expansion coefficient mismatch brought by the change in the Si3N4w volume fraction should be taken into consideration during the preparation of wave-transparent composites.


FIGURE 5. Surface morphology of 45 and 25 vol% Si3N4w/Si3N4: (A) surface crack distribution of 45 vol% Si3N4w/Si3N4; (B) surface crack width of 45 vol% Si3N4w/Si3N4; (C) surface crack distribution of 25 vol% Si3N4w/Si3N4; (D) surface morphology of 25 vol% Si3N4w/Si3N4.

Assuming the density of both Si3N4w and the Si3N4 matrix as 3.2 g/cm3, the volume fraction of whisker, matrix, open pore, and close pore of the five prepared Si3N4w/Si3N4 composites through weight, bulk density, and open porosity were all obtained. In Figure 6, the volume fractions of the solid phase of Si3N4w and the matrix were proportional to bulk densities in Figure 4. Lower Si3N4w volume fractions led to elevated relative contents of the matrix. In turn, higher relative contents of the matrix represented superior load transfer capacities.


FIGURE 6. The volume fraction of open pores, closed pores, whisker, and matrix/vol%.

Typical macromorphologies of the Si3N4w/Si3N4 samples are displayed in Figure 7. The surface of 25 vol% Si3N4w/Si3N4 looked evenly white with a hard texture (Figures 7A). The thickness of 25 vol% Si3N4w/Si3N4 was estimated to be approximately 2 mm (Figures 7B). Also, two dividing centrosymmetric lines were noticed and both estimated to 0.5 mm from the surface. This confirmed the limited penetration depth of the Si3N4 matrix in a specific gel-casting Si3N4w preform under the CVI Si3N4 process.


FIGURE 7. Typical macromorphology of Si3N4w/Si3N4: (A) surface of the 25 vol% Si3N4w/Si3N4; (B) section of the 25 vol% Si3N4w/Si3N4.

Based on the penetration morphology of Figures 7B, the structure of Si3N4w/Si3N4 was simplified as a sandwich construction. The inherent characteristics of the CVI process caused a gradual decline in the content from the surface to the dividing line. The medium part was mainly composed of Si3N4w with almost no deposited matrix. This structure was similar to the A sandwich structure of a multi-layered radome structure consisting of a high-density side layer and low-density center layer. Materials with sandwich structures often possess high specific strengths and broadband wave-transparent abilities. Meanwhile, the gradient structure of the side layers relieved the stress, which may improve the mechanical properties of the materials. In other words, the whisker preform combined with the CVI process could yield materials with A sandwich and gradient structures.

The section penetration morphologies of the five prepared Si3N4w/Si3N4 ceramics are depicted in Figure 8. Four positions (surface, 100, 500, and 1,000 μm distance from the surface) were observed for each sample, and the yellow numbers represent the thickness of the matrix around Si3N4w. The surfaces of the five prepared Si3N4w/Si3N4 were all covered by dense CVI Si3N4. Each Si3N4w/Si3N4 sample revealed that closure of the surface led to less matrix content around Si3N4w. When the surface is closed, gas cannot enter the preform through the pores, resulting in a reduction of the internal matrix phase. At the same depth, larger Si3N4w volume fractions induced less matrix content around Si3N4w. For example, matrix deposition is rarely observed at 35 and 45 vol%. With the increase of the whisker volume fraction, the amount of matrix decreases and the density changes. And the porosity increases gradually. More matrix was still deposited at 1 mm distance from the surface in 5 and 15 vol% Si3N4w/Si3N4 samples. Likewise, the density and porosity decreased, but this is exactly what is needed to form the sandwich structure mentioned later. By comparison, almost no matrix surrounded Si3N4w at only 100 μm distance from the surface in 15 vol% Si3N4w/Si3N4.


FIGURE 8. Section penetration morphology of five kinds of Si3N4w/Si3N4.

The pore size distributions of Si3N4w/Si3N4 are gathered in Figure 9. The pore sizes of all five Si3N4w/Si3N4 specimens looked normally distributed. As Si3N4w volume fraction decreased, the pore size became more concentrated at 500, 600, 800, 1,600, and 2,500 nm, respectively. Moreover, lower Si3N4w volume fractions induced wider pore size distribution ranges. Therefore, the A sandwich structure of Si3N4w/Si3N4 showed that the CVI Si3N4 process could not effectively penetrate pores smaller than 2.5 μm in a gel-casting Si3N4w preform.


FIGURE 9. Pore size distribution of Si3N4w/Si3N4.

Mechanical Properties

The flexural strengths of the five Si3N4w/Si3N4 composites were tested and the results are shown in Figure 10. As the Si3N4w volume fraction increased, the flexural strength of Si3N4w/Si3N4 first rose and then decreased. A maximum strength of 41.37 MPa was recorded with 25 vol% Si3N4w/Si3N4. The minimum flexural strength of 22.74 MPa was registered with 45 vol% Si3N4w/Si3N4. The flexural strengths of different Si3N4w/Si3N4 composites were analyzed by combining the component volume fractions shown in Figure 6 and section penetration morphologies in Figure 8. The 5 and 15 vol% Si3N4w/Si3N4 composites showed higher load transfer abilities due to elevated matrix contents. Therefore, apparent fractures of Si3N4w can still be seen at 1 mm from the surface. However, the low Si3N4w volume fractions of 5 and 15 vol% Si3N4w/Si3N4 led to relatively lower flexural strengths. For 35 and 45 vol% Si3N4w/Si3N4, although they possessed elevated Si3N4w volume fractions, their low load transfer abilities caused by low matrix content significantly decreased their flexural strengths. Furthermore, the flexural strengths of 35 and 45 vol% Si3N4w/Si3N4 were a little lower than those of 5 and 15 vol% Si3N4w/Si3N4, confirming the significant influence of the load transfer ability of the matrix on flexural strength. By contrast, the 25 vol% Si3N4w/Si3N4 ceramic integrated a moderate whisker volume fraction and matrix content, thereby inducing a better strengthening effect and load transfer ability. When the volume fraction of the matrix is too low, the matrix cannot effectively bond and disperse the load, which leads to a decrease of strength. Similarly, when the volume fraction of the whisker is too low, the ability to hinder cracks and other defects is very small and cannot play an enhancement role, resulting in the reduction of strength. However, the volume fraction of 25 vol% is in an intermediate state, which ensures the action of both the matrix and the reinforcer. This, in turn, led to the highest flexural strength.


FIGURE 10. Flexural strength of the five kinds of Si3N4w/Si3N4.

A typical fracture morphology of Si3N4w/Si3N4 is presented in Figure 11. Numerous flat sections can be seen in the low magnification SEM photo. The high magnification photo showed a smooth interface between Si3N4w and the Si3N4 matrix. Obviously, the fracture of Si3N4w/Si3N4 looked typically brittle, inferring the high bonding strength between Si3N4w and the Si3N4 matrix.


FIGURE 11. Typical fracture morphology of Si3N4w/Si3N4: (A) low magnification SEM photo; (B) high magnification SEM photo.

The fracture toughness values of the five Si3N4w/Si3N4 samples were tested by a single-notched beam method and the data are gathered in Figure 12. The high porosity and hollow sandwich structure of the composites led to very low fracture toughness values. As the Si3N4w volume fraction increased, the fracture toughness first fell and then rose. The highest value reached only 0.44 MPa m1/2 and was recorded with 45 vol% Si3N4w/Si3N4. By comparing the tendency with the component volume fraction in Figure 6, the fracture toughness was shown to positively correlate with the total solid content of Si3N4w and the Si3N4 matrix. From another perspective, the fracture toughness negatively correlated with porosity due to the very large bonding strength of the interface of Si3N4w and the Si3N4 matrix, which prevented cracks from deflection. As a result, larger porosity led to lower fraction toughness.


FIGURE 12. Fracture toughness of the five kinds of Si3N4w/Si3N4.

Dielectric Properties

The room-temperature dielectric properties of the five Si3N4w/Si3N4 specimens are shown in Figure 13. The dielectric constant ranged between 2.25 and 4.0, and was positively correlated with the total solid content in Figure 8. Therefore, the relative content of the whisker and matrix did not influence the dielectric constant very much. As the whisker volume increases, the real part of the complex dielectric constant increases. From the perspective of the microstructure, with the whisker volume increasing, the pore radius decreases, and the electromagnetic wave scattering in the pore increases. So the dielectric constant increases as the dielectric loss also increases. Also, the dielectric constant values of the Si3N4 matrix and Si3N4w were similar. The dielectric constant lines were approximately straight, showing a slight influence of frequency in the x-band on the dielectric constant.


FIGURE 13. Dielectric properties of the five kinds of Si3N4w/Si3N4.

Limited by the accuracy of the vector network analyzer during testing low-loss materials, the dielectric loss of the five Si3N4w/Si3N4 did not follow obvious rules. However, the dielectric loss of all five composites was less than 0.005, confirming excellent dielectric properties. Besides, the influences of the interface between the Si3N4 matrix and Si3N4w on dielectric loss were slight.


The effects of the Si3N4w volume fraction on the microstructures, mechanical properties, and dielectric characteristics of Si3N4w/Si3N4 were all studies in this paper and the following conclusions could be drawn:

(1) The connectivity of pores in the Si3N4wpreform prepared by the gel-casting process was good due to the small pore size which yielded Si3N4w/Si3N4 with an A sandwich structure. The relative matrix content of 5 vol% Si3N4w/Si3N4 was higher than that of 15 vol% Si3N4w/Si3N4. Higher Si3N4w volume fractions led to lower relative contents of the Si3N4 matrix and less matrix distribution at the same depth. In the sample of the volume fraction of 25 vol%, the content of the matrix and whisker was moderate, and the porosity was the lowest, which made it form an ideal sandwich structure.

(2) Since 25 vol% Si3N4w/Si3N4 integrated a relatively higher Si3N4w volume fraction and load transfer ability of the matrix, the resulting flexural strength reached the highest value of 41.37 MPa. At a distance of 100 μm from the surface, the matrix thickness around the whisker could still reach 140 nm. The high open porosity led to the low fraction toughness of Si3N4w/Si3N4. The obvious brittle fracture showed a very high interface bonding strength. Therefore, the fracture toughness of Si3N4w/Si3N4 was positively related to the total solid content. The surface of the sample with a 45 vol% whisker also reflected a high density, and the bulk density tended to be the highest. As a result, the fracture toughness of 45 vol% Si3N4w/Si3N4 was the highest (0.44 MPa m1/2).

(3) The dielectric constants of Si3N4w/Si3N4 ranged between 2.25 and 4.0, and was positively related to the total solid content. This may infer similar dielectric constants of Si3N4w and the Si3N4 matrix. Dielectric losses were all less than 0.005, showing good dielectric properties of the composites. Besides, the dielectric loss of the interface between Si3N4w and the Si3N4 matrix was slight.

Data Availability Statement

The original contributions presented in the study are included in the article/supplementary material, further inquiries can be directed to the corresponding author.

Author Contributions

CC, YL, and WY carried out the concepts, design, definition of intelectual content, literature search data acquisition, data analysis and manuscript preparation. FY, JW, and QZ provided assistance for data accuisition, data analysis and statistical analysis. CC carried out literature search data acquisition and manuscript editing. YL and WY performed manuscript review. All authors have read and approved the content of the manuscript.


This work was supported by the National Key Research and Development Program of China (No. 2018YFB1106600), the Chinese National Foundation for Natural Sciences under Contracts (No.51672217, No.51572224), and the Fundamental Research Funds for the Central Universities (No. 3102019ghxm014).

Conflict of Interest

The authors declare that the research was conducted in the absence of any commercial or financial relationships that could be construed as a potential conflict of interest.


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Keywords: Si3N4w/Si3N4 composites, gel-casting, chemical vapor infiltration, dielectric properties, mechanical properties

Citation: Chen C, Liu Y, Yue W, Ye F, Wang J and Zeng Q (2020) The Influence of Si3N4w Volume Fraction on the Microstructure and Properties of Si3N4w/Si3N4 Composites via CVI Technique. Front. Mater. 7:588716. doi: 10.3389/fmats.2020.588716

Received: 29 July 2020; Accepted: 19 October 2020;
Published: 27 November 2020.

Edited by:

Yang Bai, University of Oulu, Finland

Reviewed by:

Yan Zhang, Central South University, China
Subhasis Roy, University of Calcutta, India

Copyright © 2020 Chen, Liu, Yue, Ye, Wang and Zeng. This is an open-access article distributed under the terms of the Creative Commons Attribution License (CC BY). The use, distribution or reproduction in other forums is permitted, provided the original author(s) and the copyright owner(s) are credited and that the original publication in this journal is cited, in accordance with accepted academic practice. No use, distribution or reproduction is permitted which does not comply with these terms.

*Correspondence: Yongsheng Liu,